CN105018835A - Medium-high carbon hot rolled strip steel with excellent fine blanking performance and production method - Google Patents
Medium-high carbon hot rolled strip steel with excellent fine blanking performance and production method Download PDFInfo
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Abstract
The invention discloses medium-high carbon hot rolled strip steel with excellent fine blanking performance and a production method. The strip steel comprises chemical components in percentage by weight as follows: 0.50%-0.65% of C, 0.60%-1.50% of Si, 0.50%-1.70% of Mn, 0.0030%-0.0070% of Ca, 0.0008%-0.005% of B, 0.015%-0.030% of Als, smaller than or equal to 0.015% of P, smaller than or equal to 0.008% of S and the balance of Fe and inevitable impurities. According to the principle that the activity of carbon atoms in austenite is improved by the Si element, a fast spheroidizing annealing technology is adopted, the heat preservation time is shortened to 1h-2h at the annealing temperature, the cost is reduced, the energy is saved, and the hot rolled strip steel with the excellent blanking performance is obtained finally and is suitable for producing automobile part raw materials with complex shapes and quench hardening requirements.
Description
Technical field
The present invention relates to automobile component steel technical field, be specifically related to the excellent medium high carbon hot rolled strip of a kind of essence punching property and production method.
Background technology
The structure that Hyundai Motor component such as gear, wheel box, selector fork are dialled, leaf spring etc. has a complicated shape is progressively changed into by former casting, cutting, thermal treatment, accurately machined mode and adopts a material stamping-out with excellent stamping-out performance shaping.The steel plate feature with excellent stamping-out performance has: (1) suppresses the material crack at mould blade place to produce, and obtaining machined surface is the shear surface of more than 85%; (2) dimensional precision is good; (3) hardness evenly and suitably, namely can not too high reduction die life, again can not be too low and occur the situation of " being stained with knife ".Usually require that it is organized as Spheroidizing Annealing state, and require more than 70% Oxygen potential, heart portion segregation less than 1 grade.Obtain excellent stamping-out medium and high carbon steel general requirement and carry out Spheroidizing Annealing.
For above requirement, patent CN 101379207A discloses the excellent steel plate of a kind of punch press process and manufacture method thereof, its patent composition consists of C:0.1 ~ 0.5%, below Si:0.5%, Mn:0.2% ~ 1.5%, P, S are adjusted to proper range within; And median size is more than 10 μm and the median size being less than carbide in the ferrite of 20 μm and ferrite crystal grain is the tissue of 0.3 ~ 1.5 μm.
But, the annealing carrying out reaching 30 ~ 60h is needed after high carbon steel sheet hot rolling described in patent CN 101379207A, substantially increase production cost and reduce efficiency, simultaneously because long term annealing causes surface of steel plate Decarburized layer serious, steel for carbon content 0.4% ~ 0.5% inevitably cause through-thickness hardness uneven, thus occur the result that stamping-out declines.
Patent CN 103003463A discloses the excellent high-carbon hot-rolled steel sheet of a kind of fine-edge blanking and manufacture method thereof, and its patent composition (% by weight) is C:0.10 ~ 0.40%, Si; Less than 1.0%, below Mn:2.0% and surplus are by Fe and inevitable impurity forming of forming, and have proeutectoid ferrite area occupied rate in organized whole and be less than 10% and the Oxygen potential of carbide is the microstructure of more than 50%.What it was recorded is the hot-rolled steel sheet of the state of batching, and requires that steel band is cooled to the cooling stopping temperature of (nose) temperature range 450 ~ 600 DEG C from the cooling temperature of more than 650 DEG C of austenite one phase with the average cooling rate of 50 DEG C/more than s.And batch in 3s, batch rear hot rolled coil and buckle stay-warm case rapidly, utilize heat of phase transformation to promote carbide spheroidization.
But, method described by patent CN 103003463A adopts stay-warm case slow cooling, coil of strip internal-external temperature difference is larger, cooling rate difference is also large, therefore the lumber recovery of the steel band of the performance reached required by right can be caused not high, the simultaneously Oxygen potential that obtains of the method only more than 50%, for stamping-out steel plate, Oxygen potential is too low.
Summary of the invention
Object of the present invention, be to overcome above-mentioned deficiency, medium high carbon hot rolled strip and production method that a kind of essence punching property is excellent are provided, pass through Composition Design, coordinate the control of rolling technological parameter, Si element is utilized to improve the principle of carbon atom activity in austenite, adopt Quick spheroidizing annealing technology, under annealing temperature, soaking time foreshortens to 1h ~ 2h, reduce costs, save the energy, finally obtain the hot rolled strip of stamping-out excellent property, be applicable to produce the automobile component raw material that there are complicated shape and needs and harden.
For achieving the above object, the invention provides the medium high carbon hot rolled strip that a kind of essence punching property is excellent, its special character is: in described band steel, chemical composition and weight percentage are: C:0.50 ~ 0.65%, Si:0.60 ~ 1.50%, Mn:0.50 ~ 1.70%, Ca:0.0030 ~ 0.0070%, B:0.0008 ~ 0.005%, Als:0.015 ~ 0.030%, P≤0.015%, S≤0.008%, all the other are Fe and inevitable impurity.
Preferably, in described band steel, chemical composition and weight percentage are: C:0.50 ~ 0.60%, Si:0.70 ~ 1.50%, Mn:0.70 ~ 1.20%, Ca:0.0030 ~ 0.0070%, B:0.0008 ~ 0.005%, Als:0.015 ~ 0.025%, P≤0.015%, S≤0.008%, all the other are Fe and inevitable impurity.
Preferably, in described band steel, chemical composition and weight percentage are: C:0.55 ~ 0.60%, Si:1.0 ~ 1.20%, Mn:1.20 ~ 1.60%, Ca:0.0030 ~ 0.0070%, B:0.0008 ~ 0.005%, Als:0.015 ~ 0.020%, P≤0.015%, S≤0.008%, all the other are Fe and inevitable impurity.
The present invention also provides the production method of the medium high carbon hot rolled strip that above-mentioned essence punching property is excellent, and its special character is: comprise the steps:
1) smelt also continuous casting and become base;
2) carry out slow cooling to strand, the slow cooling time is not less than 72 hours;
3) to strand heating, heating and temperature control is at 1200 ~ 1280 DEG C, and time inside furnace is at 300 ~ 400min;
4) high-pressure water descaling is carried out;
5) hot rolling is carried out: control roughing end temp at 980 ~ 1100 DEG C, draft is not less than 80%; Control finish rolling finishing temperature at A
c3+ 30 DEG C ~ A
c3within the scope of+80 DEG C, draft is not less than 65%;
6) adopt front end cooling, it is 30 ~ 80 DEG C/s that speed of cooling controls, and the temperature controlling to stop cooling is 600 DEG C ~ 700 DEG C;
7) batch, coiling temperature is 570 ~ 650 DEG C, and now metallographic structure is: perlite is not less than 90%, and surplus is ferrite;
8) after As rolled coil of strip air cooling to room temperature, carry out Spheroidizing Annealing through perhydro formula bell type annealing furnace, concrete steps are: first heat coil of strip to its heart portion temperature at A
c1-25 DEG C ~ A
c1within the scope of-5 DEG C, be then incubated 60min, below furnace cooling to 550 DEG C, air cooling of coming out of the stove is to room temperature;
In above-mentioned steps, A
c3, A
c1unit be DEG C obtained by following two formulae discovery respectively:
Ac
1＝723+25Si-7Mn；
In above-mentioned two formula, C, Mn, Si represent the value of wt in the wt% (weight percentage) that these elements are shared separately.
Below describe the reason of selected alloying element, composition range and key process parameter in the present invention.
C: content controls in 0.50% ~ 0.65% scope.The element of the hardness strength after carbon remarkably influenced hot-roll annealing and after quenching, needs carbon content control 0.25% ~ 0.55% in the present invention.Can not obtain the hardness needed for automobile and work machine parts during carbon < 0.25%, As rolled tissue easily obtains more proeutectoid ferrite; During carbon > 0.65%, even if Oxygen potential reaches more than 80%, still hardening after steel plate annealing, damages mould or cracks when can not guarantee that essence is rushed.Therefore, carbon is limited to 0.50% ~ 0.65%.
Si: content controls in 0.60% ~ 1.50% scope.The Main Function that silicon plays in the present invention is the effect improving carbon atom activity in austenite significantly, as silicon > 0.6%, comparatively can significantly improve the activity of carbon atom during Spheroidizing Annealing temperature thus greatly reduce the Spheroidizing Annealing time, but element silicon can play the effect of significant hardened Fe ferritic thus worsen stamping-out performance, therefore controls silicon < 1.5%.Therefore, limiting silicone content is 0.60% ~ 1.50%.
Mn: content controls 0.50% ~ 1.70%, is the important element improving steel plate hardening capacity and wear resistance, expands austenite phase field, can suitably reduce Spheroidizing Annealing temperature.The higher meeting of Fe content causes more serious center segregation and reduces toughness, and manganese is chosen as 0.50% ~ 1.70%.
Ca: content controls 0.0030% ~ 0.0070%, the calcium of trace makes sulfide inclusion nodularization, improves steel band toughness.The calcium of trace promotes the Grain Boundary Segregation of carbon simultaneously, makes proeutectoid ferrite at the more difficult forming core of austenite grain boundary, thus plays the effect suppressing proeutectoid ferrite.It is 0.0030% ~ 0.0070% that calcium contents is selected in
B: content controls the scope 0.0008% ~ 0.005%, be segregation on austenite boundary, trace can significantly improve hardenability element.In order to improve hardenability, need the content of more than 0.0008%, content is more than 0.005% on the other hand, and effect is saturated, cannot continue to improve hardenability, generates boron phase on the contrary thus worsens the performances such as steel plate extension.Therefore boron is preferably defined as the scope of 0.0008% ~ 0.005%.
Als: content controls 0.010 ~ 0.030% is effective deoxidant element, but also plays the base metal tenacity raising effect brought by making the microstructure thinning of steel plate.Aluminium content will more than 0.030%, but aluminium too high levels is easy to oxygen forms the larger erose Al of wedge angle of particle
2o
3, base metal tenacity is worsened.Therefore aluminium content is limited to 0.015% ~ 0.030%.
In technique scheme, Ac
3and Ac
1calculation formula first as follows:
Ac
1＝723+25Si-7Mn+15Cr-15Ni+50V+40Mo；
Because in the chemical composition in band steel of the present invention, Cr, Ni, Mo, V element do not occur, so be reduced to:
Ac
1＝723+25Si-7Mn；
In above-mentioned two formula, C, Mn, Si represent the value of wt in the wt% (weight percentage) that these elements are shared separately.
Finish rolling finish to gauge end temp of the present invention controls at A
c3+ 30 DEG C ~ A
c3+ 80 DEG C.Reason is: if finish to gauge end temp is higher than A
c3when+80 DEG C, the rusty scale of generation is thickening, coarse grains, crystal boundary total surface area reduces, and the globular carbide dispersity formed after Spheroidizing Annealing declines, and original austenite grain is thick on the other hand, the martensite silver formed after causing final quenching is thick, reduces part use properties; If finish to gauge end temp is lower than A
c3when+30 DEG C, steel plate in finish to gauge to laminar cooling process temperature drop to A
c3below, the proeutectoid ferrite scale of construction can be caused to increase, the end temp of finish to gauge is simultaneously too low, causes rolling loads to increase, and plate shape is difficult to control.
Finish to gauge of the present invention terminates rear speed of cooling and controls to be 30 ~ 80 DEG C/s.Reason is: if after finish to gauge during rate of cooling < 30 DEG C/s, is difficult to the generation ensureing to suppress proeutectoid ferrite; And if after finish to gauge during rate of cooling > 80 DEG C/s, as easy as rolling off a log bainite tissue or martensitic stucture, make the As rolled hardening of tissue, when batching, load increases, and after steel strip coiling, edge cracks.
The temperature that the present invention controls to stop cooling is 600 DEG C ~ 700 DEG C.Reason is: be the steel of 0.50% ~ 0.65% for carbon content, be quasi-eutectoid perlitic transformation district in this temperature range, if final cooling temperature > 700 DEG C, easily forms Ferrite Strip Structure in follow-up process of cooling, because Structure Inheritance effect Oxygen potential is not high; If final cooling temperature < 600 DEG C, then likely there is bainite transformation in local in steel plate, causes uneven microstructure, medium and high carbon steel is increased to the difficulty of longitudinal shearing slitting, very easily rupture when subsequent user trimming and slitting.
Oiler temperature control of the present invention is at 570 ~ 650 DEG C.Reason is: if when coiling temperature is higher than 650 DEG C, easily make coil of strip local temperature more than A under batching latent heat of phase change effect subsequently
c1, cause generating proeutectoid ferrite, after Spheroidizing Annealing, because Structure Inheritance effect Oxygen potential is not high; If when coiling temperature is lower than 570 DEG C, coil of strip easily forms bainite or martensite end to end, and material is hardened, and is unfavorable for following process.
Coils of hot-rolled steel of the present invention, through bell furnace Spheroidizing Annealing, when coil of strip heart portion, temperature reaches A
c1-25 DEG C ~ A
c1when-5 DEG C, soaking time is 1h, and below furnace cooling to 550 DEG C, air cooling of coming out of the stove is to room temperature.This is owing to working as Heating temperature lower than A
c1when-25 DEG C, the Spheroidizing Annealing of short period of time insulation, can not reach best nodularization effect; And when temperature is higher than A
c1when-5 DEG C, easily cause coil of strip local temperature too high, form sheet pearlitic structure.
Beneficial effect of the present invention:
(1) the medium high carbon hot rolled strip that the stamping-out of the short annealing of the present invention's production is excellent, adopts medium and high carbon steel Composition Design, does not add the precious alloys such as Ni, Mo, Cu, reduce production cost.
(2) add Ca and improve sulfide inclusion on the one hand as alloy element, the more important thing is that Ca promotes that C is to grain boundary segregation, is aided with certain front end cooling way, thus inhibits the generation of proeutectoid ferrite preferably.
(3) add more Si as carbon atom activity in raising austenite, thus make to be conducive to pearlitic spheroidization in annealing region, greatly shorten the Spheroidizing Annealing time, reduce costs, save the energy.
(4) control slab heating temperature, finishing temperature, coiling temperature, stronger front end cooling system, thus reach the suppression generation of proeutectoid ferrite and the effect of crystal grain thinning.
(5) due to the control to As rolled tissue, even if also obtain the such tissue of proeutectoid ferrite+fine and closely woven perlite of less than 8% in the steel of C content 0.25%, namely the preparation tissue of Spheroidizing Annealing is conducive to, within the scope of annealing holding temperature, due to the effect compared with high Si content, carbide spheroidization is completed rapidly, and globular carbide is uniformly distributed in the base simultaneously, and after annealing, each position of entire volume steel band all can form uniform globular pearlite tissue.The globular pearlite that whole thickness of strips cross section is evenly distributed, there is excellent Blanking Properties and hardening capacity, the over-all properties of this invention medium and high carbon steel is stablized, yield strength ReL≤500MPa, tensile strength Rm≤650MPa, unit elongation >=20%, the two-sided total decarburized layer degree of depth≤1.5d (d is thickness), tissue signature is: As rolled proeutectoid ferrite phase control is below 8%, in annealed state ferrite crystal grain, the median size of carbide is the tissue of 0.3 ~ 1.5 μm, and carbide spheroidization rate is the microstructure of more than 80%.
Accompanying drawing explanation
Fig. 1 is the embodiment of the present invention 6 As rolled typical organization figure;
Fig. 2 is typical organization figure after the embodiment of the present invention 6 Spheroidizing Annealing.
Embodiment
Below in conjunction with the drawings and specific embodiments, the present invention is described in further detail:
Chemical composition design:
In band steel, chemical composition and weight percentage are: C:0.50 ~ 0.65%, Si:0.60 ~ 1.50%, Mn:0.50 ~ 1.70%, Ca:0.0030 ~ 0.0070%, B:0.0008 ~ 0.005%, Als:0.015 ~ 0.030%, P≤0.015%, S≤0.008%, all the other are Fe and inevitable impurity.
Technical process is as follows:
1) smelt also continuous casting and become base;
2) carry out slow cooling to strand, the slow cooling time is not less than 72 hours;
3) to strand heating, heating and temperature control is at 1200 ~ 1280 DEG C, and time inside furnace is at 300 ~ 400min;
4) high-pressure water descaling is carried out;
5) hot rolling is carried out: control roughing end temp at 980 ~ 1100 DEG C, draft is not less than 80%; Control finish rolling finishing temperature at A
c3+ 30 DEG C ~ A
c3within the scope of+80 DEG C, draft is not less than 65%;
6) adopt front end cooling, it is 30 ~ 80 DEG C/s that speed of cooling controls, and the temperature controlling to stop cooling is 600 DEG C ~ 700 DEG C;
7) batch, coiling temperature is 570 ~ 650 DEG C, and now metallographic structure is: perlite is not less than 90%, and surplus is ferrite;
8) after As rolled coil of strip air cooling to room temperature, carry out Spheroidizing Annealing through perhydro formula bell type annealing furnace, concrete steps are: first heat coil of strip to its heart portion temperature at A
c1-25 DEG C ~ A
c1within the scope of-5 DEG C, be then incubated 60min, below furnace cooling to 550 DEG C, air cooling of coming out of the stove is to room temperature;
In above-mentioned steps, A
c3, A
c1unit be DEG C obtained by following two formulae discovery respectively:
Ac
1＝723+25Si-7Mn；
In above-mentioned two formula, C, Mn, Si represent the value of wt in the wt% (weight percentage) that these elements are shared separately.
Each embodiment smelts 220 ~ 250mm heavy slab by above-mentioned chemical composition design requirement and technical process, the requirement of specific chemical composition value and related process parameters according to the form below 1 and table 2 is respectively carried out, the last test film getting 100mm × 100mm from gained steel plate, use the oil press of 100 tons at gap (thickness of slab 1%), operating force is 8.5 tons, the condition undershoot of lubrication is had to make arrangement after due consideration the steel billet of 20mm × 80mm, be more than 85% shear surface by stamping-out end face, and end face does not have the average evaluation of crackle be √, by average evaluation be in addition ×.
The value list (wt%) of table 1 various embodiments of the present invention and comparative example
The main technologic parameters of table 2 various embodiments of the present invention and comparative example and the results list
As seen from Table 2, under Fast Spheroidizing Annealing condition, embodiment of the present invention steel has excellent stamping-out, and after annealing, carbide spheroidization rate is high, and comparative example 1 is due to Si too high levels, and ferrite still hardening after causing annealing, occurs crackle during stamping-out.Comparative example 2 is because Si is containing quantity not sufficient, and after taking Fast Spheroidizing Annealing, Oxygen potential is too low, stamping-out degradation.Comparative example 3 is too low owing to rolling rear cooling rate, causes coiling temperature higher, has occurred proeutectoid ferrite in steel, and after causing annealing, in steel, nodularization is uneven, and Oxygen potential is not high, stamping-out performance inconsistency lattice.Comparative example 4 due to temperature during Spheroidizing Annealing too high, organize complete austenitizing, occurred lamellar pearlite tissue in steel after short period of time heating cooling, Oxygen potential declines.Comparative example 5 due to temperature during Spheroidizing Annealing too low, change motivating force inadequate, cause quasi-eutectoid perlite in steel to have little time all to change spherical and granular carbide into, after short period of time heating cooling, in steel, Oxygen potential does not reach more than 80% requirement, stamping-out degradation.
And Fig. 1, Fig. 2 also can find out that the embodiment of the present invention 6 obtains typical organization after As rolled typical organization and Spheroidizing Annealing, show the destination organization required for obtaining, reach requirement.
Above-described embodiment is only the best and exemplifies, and is not the restriction to embodiments of the present invention.
Claims (4)
1. the medium high carbon hot rolled strip that an essence punching property is excellent, it is characterized in that: in described band steel, chemical composition and weight percentage are: C:0.50 ~ 0.65%, Si:0.60 ~ 1.50%, Mn:0.50 ~ 1.70%, Ca:0.0030 ~ 0.0070%, B:0.0008 ~ 0.005%, Als:0.015 ~ 0.030%, P≤0.015%, S≤0.008%, all the other are Fe and inevitable impurity.
2. the medium high carbon hot rolled strip that essence punching property according to claim 1 is excellent, it is characterized in that: in described band steel, chemical composition and weight percentage are: C:0.50 ~ 0.60%, Si:0.70 ~ 1.50%, Mn:0.70 ~ 1.20%, Ca:0.0030 ~ 0.0070%, B:0.0008 ~ 0.005%, Als:0.015 ~ 0.025%, P≤0.015%, S≤0.008%, all the other are Fe and inevitable impurity.
3. the medium high carbon hot rolled strip that essence punching property according to claim 1 is excellent, it is characterized in that: in described band steel, chemical composition and weight percentage are: C:0.55 ~ 0.60%, Si:1.0 ~ 1.20%, Mn:1.20 ~ 1.60%, Ca:0.0030 ~ 0.0070%, B:0.0008 ~ 0.005%, Als:0.015 ~ 0.020%, P≤0.015%, S≤0.008%, all the other are Fe and inevitable impurity.
4. a production method for the medium high carbon hot rolled strip that essence punching property according to claim 1 is excellent, is characterized in that: comprise the steps:
1) smelt also continuous casting and become base;
2) carry out slow cooling to strand, the slow cooling time is not less than 72 hours;
3) to strand heating, heating and temperature control is at 1200 ~ 1280 DEG C, and time inside furnace is at 300 ~ 400min;
4) high-pressure water descaling is carried out;
5) hot rolling is carried out: control roughing end temp at 980 ~ 1100 DEG C, draft is not less than 80%; Control finish rolling finishing temperature at A
c3+ 30 DEG C ~ A
c3within the scope of+80 DEG C, draft is not less than 65%;
6) adopt front end cooling, it is 30 ~ 80 DEG C/s that speed of cooling controls, and the temperature controlling to stop cooling is 600 DEG C ~ 700 DEG C;
7) batch, coiling temperature is 570 ~ 650 DEG C, and now metallographic structure is: perlite is not less than 90%, and surplus is ferrite;
8) after As rolled coil of strip air cooling to room temperature, carry out Spheroidizing Annealing through perhydro formula bell type annealing furnace, concrete steps are: first heat coil of strip to its heart portion temperature at A
c1-25 DEG C ~ A
c1within the scope of-5 DEG C, be then incubated 60min, below furnace cooling to 550 DEG C, air cooling of coming out of the stove is to room temperature;
In above-mentioned steps, A
c3, A
c1unit be DEG C obtained by following two formulae discovery respectively:
Ac
1＝723+25Si-7Mn；
In above-mentioned two formula, C, Mn, Si represent the value of wt in the wt% (weight percentage) that these elements are shared separately.
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| CN105543647A (en) * | 2015-12-15 | 2016-05-04 | 安徽楚江特钢有限公司 | High-strength special steel alloy and preparation process thereof |
| CN105543646A (en) * | 2015-12-15 | 2016-05-04 | 安徽楚江特钢有限公司 | Production process for medium-high carbon steel through thin slabs |
| CN106424193A (en) * | 2016-09-21 | 2017-02-22 | 唐山国丰钢铁有限公司 | Manufacturing method of hot rolled strip steel of hypereutectoid spheroidized pearlite structure |
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| CN105543646A (en) * | 2015-12-15 | 2016-05-04 | 安徽楚江特钢有限公司 | Production process for medium-high carbon steel through thin slabs |
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| CN107201436A (en) * | 2017-05-08 | 2017-09-26 | 武汉钢铁有限公司 | A kind of process for producing Thin Specs medium carbon steel |
| CN107746932A (en) * | 2017-12-06 | 2018-03-02 | 东北大学 | A kind of preparation method of GCr15 bearing steels |
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| CN111054746A (en) * | 2019-12-31 | 2020-04-24 | 佛山市高明基业冷轧钢板有限公司 | Cold rolling production process of high-carbon steel |
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| CN113832311A (en) * | 2021-09-30 | 2021-12-24 | 北京科技大学 | Method for producing rapid spheroidizing special steel |
| CN115747666A (en) * | 2023-01-10 | 2023-03-07 | 山西建龙实业有限公司 | Low-carbon hot-rolled pickled steel and control method for transverse crease mark defects of steel strip of low-carbon hot-rolled pickled steel |
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